JPH059509A - Sintered body of high-alloy tool steel and production thereof - Google Patents
Sintered body of high-alloy tool steel and production thereofInfo
- Publication number
- JPH059509A JPH059509A JP3187052A JP18705291A JPH059509A JP H059509 A JPH059509 A JP H059509A JP 3187052 A JP3187052 A JP 3187052A JP 18705291 A JP18705291 A JP 18705291A JP H059509 A JPH059509 A JP H059509A
- Authority
- JP
- Japan
- Prior art keywords
- tool steel
- alloy tool
- powder
- sintered body
- mixed
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 49
- 239000000956 alloy Substances 0.000 title claims abstract description 49
- 229910001315 Tool steel Inorganic materials 0.000 title claims abstract description 38
- 238000004519 manufacturing process Methods 0.000 title claims description 6
- 239000000843 powder Substances 0.000 claims abstract description 54
- 239000007790 solid phase Substances 0.000 claims abstract description 8
- 239000000203 mixture Substances 0.000 claims description 10
- 238000005245 sintering Methods 0.000 abstract description 23
- 239000000463 material Substances 0.000 abstract description 19
- 230000007547 defect Effects 0.000 abstract description 10
- 150000001247 metal acetylides Chemical class 0.000 abstract description 6
- 230000015572 biosynthetic process Effects 0.000 abstract description 4
- 239000013078 crystal Substances 0.000 abstract description 4
- 239000010419 fine particle Substances 0.000 abstract description 4
- 239000011362 coarse particle Substances 0.000 abstract description 3
- 238000002844 melting Methods 0.000 abstract description 3
- 230000008018 melting Effects 0.000 abstract description 3
- 230000007847 structural defect Effects 0.000 abstract description 3
- 238000000465 moulding Methods 0.000 abstract description 2
- 230000004931 aggregating effect Effects 0.000 abstract 1
- 239000002245 particle Substances 0.000 description 7
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 6
- 238000002156 mixing Methods 0.000 description 5
- 238000000034 method Methods 0.000 description 4
- 238000010586 diagram Methods 0.000 description 3
- 238000004663 powder metallurgy Methods 0.000 description 3
- 238000005054 agglomeration Methods 0.000 description 2
- 230000002776 aggregation Effects 0.000 description 2
- 238000005520 cutting process Methods 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 238000005242 forging Methods 0.000 description 2
- 239000007791 liquid phase Substances 0.000 description 2
- 239000011148 porous material Substances 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- SDGKUVSVPIIUCF-UHFFFAOYSA-N 2,6-dimethylpiperidine Chemical compound CC1CCCC(C)N1 SDGKUVSVPIIUCF-UHFFFAOYSA-N 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 238000000280 densification Methods 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 238000001778 solid-state sintering Methods 0.000 description 1
Landscapes
- Powder Metallurgy (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】この発明は、材料内部の微少欠陥
等が問題となる切削工具用の高合金工具鋼焼結体及びそ
の製造法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a high alloy tool steel sintered body for a cutting tool in which minute defects and the like inside the material pose a problem, and a method for producing the same.
【０００２】[0002]
【従来の技術】粉末冶金法により高合金工具鋼焼結体を
製造するには、ＣＩＰ装置を用いて圧粉体を成形しその
後焼結したり、あるいはＨＩＰ装置を用いて直接焼結体
を製造し、更にこの焼結体に鍛造、圧延等の塑性加工を
加え、目的に応じて丸材、角材、板材及び線材、或いは
所望の工具形状等に加工製造されている。かかる高合金
工具鋼粉末焼結体に塑性加工を必要とするのは、通常焼
結体には空隙、空孔等の欠陥があり、完全に緻密な焼結
体を得ることは困難であるからであり、かかる焼結体に
塑性加工を施してこれらを押しつぶし、空隙等の欠陥を
改善して完全緻密化を計ることが必要である。2. Description of the Related Art In order to produce a high alloy tool steel sintered body by powder metallurgy, a CIP device is used to form a green compact and then sintered, or a HIP device is used to directly produce a sintered body. After being manufactured, the sintered body is further subjected to plastic working such as forging and rolling to be processed into a round material, a square material, a plate material and a wire material, or a desired tool shape according to the purpose. Such high alloy tool steel powder sinter requires plastic working, because normally sinter has defects such as voids and holes, and it is difficult to obtain a completely dense sinter. Therefore, it is necessary to subject such a sintered body to plastic working to crush these to improve defects such as voids and to achieve complete densification.
【０００３】例えば、粉末冶金法を用いる原料粉末には
一般的に粉粒径が101 〜103 μｍ未満の粗粒粉或いは超
微粉、ナノ微粉といわれる粉粒径が101 未満で〜10-2μ
ｍの粉末がそれぞれ単独で使われている。粗粒粉は圧粉
体の成形時に空隙ができやすく、焼結時にこれらの空隙
を除去して完全緻密化することは極めて困難である。ま
た超微粉単独で圧粉体を成形する場合は、圧粉体の相対
密度が高くなり過ぎるため、孤立空隙ができやすく、焼
結後微細な空孔として残留する。For example, a raw material powder produced by powder metallurgy generally has a particle size of 10 1 to less than 10 3 μm, a coarse particle or ultrafine powder, and a nanofine powder having a particle size of less than 10 1 to 10 10. -2 μ
m powders are used individually. Coarse-grained powder tends to have voids during compacting, and it is extremely difficult to remove these voids during sintering to completely densify. Further, in the case of molding a green compact by using only ultrafine powder, the relative density of the green compact becomes too high, so that isolated voids are easily formed, and fine voids remain after sintering.
【０００４】[0004]
【発明が解決しようとする課題】本来、粉末冶金法の最
も特徴とするところは、高い形状の自由度を有している
ところにある。このため、高合金工具鋼の粉末を例えば
丸材、角材、板材は勿論のこと、ドリル、エンドミル等
の所望の工具形状の圧粉体に成形することも極めて容易
である。その反面、焼結によって空孔等の材料欠陥が内
部に残留することは不可避である。しかし、これらの欠
陥を皆無にして完全に緻密化することは極めて困難であ
り、切削工具では材料内部の欠陥に基づくチッピング、
欠損等が使用上問題となり、十分な工具性能は期待でき
ない。従って工具製品形状の焼結体で実用化するには至
っているものは殆どないのが現状である。Originally, the most characteristic feature of the powder metallurgy method is that it has a high degree of freedom in shape. For this reason, it is extremely easy to form powder of high alloy tool steel into not only round material, square material, plate material, but also a green compact having a desired tool shape such as a drill and an end mill. On the other hand, it is inevitable that material defects such as voids remain inside due to sintering. However, it is extremely difficult to completely densify these defects, and with cutting tools, chipping due to defects inside the material,
Defects become a problem in use, and sufficient tool performance cannot be expected. Therefore, in the present situation, there is almost no sintered product having a tool product shape that has been put to practical use.
【０００５】一方、圧粉体を成形後、焼結温度を高くす
ることによって空孔等の欠陥は減少する傾向を示し、液
相焼結においては気孔の残留が殆ど認められず、相対密
度が１００％に近い焼結体を得ることが可能であるが、
結晶粒の粗大化や炭化物の溶融、凝集に伴う巨大炭化物
の形成等の材料的な組織欠陥を生じて材料の強靱性及び
工具性能を著しく劣化させることになる。また、高合金
工具鋼は、前記従来技術のように塑性加工を施して空隙
等の欠陥を改善するものであるから、材料の歩留りが悪
く、また多大の加工工数を必要とするのであり、きわめ
て高価となるという問題もあった。On the other hand, defects such as voids tend to decrease by raising the sintering temperature after compacting the green compact, and in the liquid phase sintering, almost no residual pores are recognized and the relative density is It is possible to obtain a sintered body close to 100%,
Material structural defects such as coarsening of crystal grains, melting of carbides, formation of giant carbides due to agglomeration, etc. occur, and the toughness of the material and the tool performance are significantly deteriorated. Further, the high alloy tool steel is to improve the defects such as voids by subjecting it to plastic working as in the prior art, so that the yield of the material is poor, and a large number of working man-hours are required. There was also the problem of becoming expensive.
【０００６】[0006]
【課題を解決するための手段】この発明は、粒径が101
〜103 μｍ未満の高合金工具鋼の粗粒粉８０〜２０重量
％に、粒径が101 未満で10-2μｍまでの高合金工具鋼の
微粒粉を２０〜８０％含み、相対密度１００％の緻密特
性を有する高合金工具鋼焼結体、及び粒径が101 〜103
μｍ未満の高合金工具鋼の粗粒粉８０〜２０重量％に、
粒径が101 μｍ未満で10-2μｍまでの高合金工具鋼の微
粒粉を２０〜８０％配合し、次いでこれを圧粉成形し、
さらに真空雰囲気中で１５０３〜１５７３Ｋの温度で約
１２０分間固相焼結処理し、相対密度１００％の緻密特
性を得ることを特徴とする高合金工具鋼焼結体の製造方
法に係わり、粉末冶金法の特徴である形状の自由度を維
持すると共に、材料の緻密化を実現したものである。The present invention has a particle size of 10 1
Approximately 80 to 20% by weight of coarse powder of high alloy tool steel of less than -10 3 μm and 20 to 80% of fine powder of high alloy tool steel with a particle size of less than 10 1 and up to 10 -2 μm. High alloy tool steel sintered body having 100% denseness characteristics and grain size of 10 1 to 10 3
80 to 20% by weight of coarse powder of high alloy tool steel of less than μm,
20-80% of fine powder of high alloy tool steel having a grain size of less than 10 1 μm and up to 10 −2 μm is blended, and then this is compacted,
Further, it relates to a method for producing a high alloy tool steel sintered body, which is characterized by obtaining a dense characteristic with a relative density of 100% by performing a solid phase sintering treatment at a temperature of 1503 to 1573K in a vacuum atmosphere for about 120 minutes. While maintaining the degree of freedom in shape, which is a feature of the law, the material has been densified.
【０００７】本発明において、粗粒径を101 〜103 μｍ
未満としたのは、103 μｍ以上では組織、炭化物及び結
晶粒が粗大となり、材料の強度劣化の原因となるからで
あり、また微粒径を101 未満で10-2μｍまでとしたの
は、10-2μｍは技術的に製造可能な限界値であるからで
ある。In the present invention, the coarse particle size is 10 1 to 10 3 μm.
The reason for this is that if it is 10 3 μm or more, the structure, carbides, and crystal grains become coarse, which causes deterioration of the strength of the material. Also, the fine particle size is less than 10 1 and up to 10 -2 μm. Is because 10 −2 μm is a technically manufacturable limit value.
【０００８】[0008]
【実施例】次に、本発明に係る実施例を説明する。図１
は表１にＨ１乃至Ｈ６として示す各種の合金粉末の比較
的粗い粒粉の高合金工具鋼成分を混合した各種の高合金
工具鋼粉末であり、図１の上段は相対密度５４質量％、
図１の下段は８４質量％の圧粉体のそれぞれの焼結温度
と焼結体の相対密度の関係を示したものである。いずれ
も、真空炉で９×１０-1〜１０-5の真空度で１２０分間
固相焼結したものである。EXAMPLES Next, examples of the present invention will be described. Figure 1
Are various high-alloy tool steel powders obtained by mixing high-alloy tool steel components of relatively coarse-grained powders of various alloy powders shown as H1 to H6 in Table 1. The upper part of FIG.
The lower part of FIG. 1 shows the relationship between the respective sintering temperatures of the 84 mass% green compact and the relative density of the sintered body. All of them were solid-phase sintered in a vacuum furnace at a vacuum degree of 9 × 10 −1 to 10 −5 for 120 minutes.
【０００９】焼結体の相対密度は、成分組成及び圧粉体
の密度によって異なるが、圧粉体の密度５４％では、Ｈ
１＝１４７３Ｋ，Ｈ２＝１５４７Ｋ，Ｈ３＝１５２３
Ｋ，Ｈ４＝１５５０Ｋ，Ｈ５＝１５０３Ｋ，Ｈ６＝１５
３３Ｋの焼結温度で相対密度１００％の焼結体が得られ
るのに対し、圧粉体の密度８４％では、Ｈ１＝１４７３
Ｋ，Ｈ２＝１５２３Ｋ，Ｈ３＝１５０３Ｋ，Ｈ４＝１５
４７Ｋ，Ｈ５＝１５０３Ｋ，Ｈ６＝１４７３Ｋで、相対
密度１００％の焼結体が得られ、Ｈ１，Ｈ５成分のもの
を除き、圧粉体の密度の高い方が低い焼結温度で相対密
度の高い焼結体が得られることが示される。また、焼結
温度が高くなると相対密度が高くなる傾向も同時に示す
もので、このことは成分組成の液相温度の高低も関連し
ているものと考えられる。この場合、比較のために水素
雰囲気による固相焼結を行ったところ、相対密度が９５
〜９７％で飽和または最大となり、少量の孤立空隙が残
留することが確認された。The relative density of the sintered body varies depending on the component composition and the density of the green compact.
1 = 1473K, H2 = 1547K, H3 = 1523
K, H4 = 1550K, H5 = 1503K, H6 = 15
A sintered body having a relative density of 100% can be obtained at a sintering temperature of 33 K, while H1 = 1473 when the density of the green compact is 84%.
K, H2 = 1523K, H3 = 1503K, H4 = 15
47K, H5 = 1503K, H6 = 1473K, a sintered body having a relative density of 100% is obtained. Except for the H1 and H5 components, the green compact having a higher density has a higher relative density at a lower sintering temperature. It is shown that a sintered body is obtained. In addition, there is a tendency for the relative density to increase as the sintering temperature increases, which is considered to be related to the high and low liquidus temperatures of the component compositions. In this case, when solid phase sintering was performed in a hydrogen atmosphere for comparison, the relative density was 95%.
It was confirmed that it was saturated or maximum at ˜97%, and a small amount of isolated voids remained.
【００１０】[0010]
【表１】 [Table 1]
【００１１】相対密度１００％に至る焼結温度は成分配
合によって異なるが、表１のＨ２の合金粉末を焼結する
場合では１５２３〜１５５０Ｋ、Ｈ４では１５５０Ｋで
ある。特にＨ４の合金粉末では液相に近い高温焼結で相
対密度１００％が得られた。本発明により得られた焼結
体の相対密度の一例を図２及び図３に示す。図２は表１
の合金成分中のＨ２について粉粒径１０1 未満〜１０-2
μｍのＦｅ微粒粉（カーボニル鉄粉）を用い、その他の
成分は各単独元素の粗粒粉を混合したときのＦｅ微粒粉
の混合量と相対密度の関係を示したものである。この場
合、１５０３Ｋ×７．２Ｋｓの固相焼結においてＦｅ微
粉４０％質量％で相対密度１００％が得られた。The sintering temperature up to a relative density of 100% varies depending on the composition of the components, but is 1523 to 1550K in the case of sintering the H2 alloy powder in Table 1, and 1550K in the case of H4. Particularly, with the H4 alloy powder, a relative density of 100% was obtained by high temperature sintering close to the liquid phase. An example of the relative density of the sintered body obtained by the present invention is shown in FIGS. 2 and 3. Figure 1 shows Table 1
Regarding H2 in the alloy components of, powder particle size less than 10 1 to 10 -2
A micronized Fe fine powder (carbonyl iron powder) is used, and the other components show the relationship between the amount of fine Fe powder mixed and the relative density when coarse powders of individual elements are mixed. In this case, a relative density of 100% was obtained with 40% by mass of Fe fine powder in solid phase sintering of 1503K × 7.2Ks.
【００１２】図３は表１中の本発明に係わるＨ４の高合
金工具鋼について、高合金工具鋼と同一成分の合金粗粒
粉に高合金工具鋼を成分組成とする単独元素の７種の微
粒粉を混合したときの相対密度の関係を示したものであ
る。圧粉体の相対密度が８４％のものは、微粉末の混合
量が２０質量％、５４％のものは４０質量％、焼結温度
が１５２３Ｋ×７．２Ｋｓの固相焼結において、相対密
度が１００％の焼結体が得られた。FIG. 3 shows the high alloy tool steel of H4 according to the present invention in Table 1, in which 7 kinds of single elements having the same composition as the high alloy tool steel and the coarse alloy powder having the same composition as the high alloy tool steel are used. It shows the relationship of relative density when fine powder is mixed. When the relative density of the green compact is 84%, the mixing amount of the fine powder is 20% by mass, that of 54% is 40% by mass, and the relative density in the solid-phase sintering at the sintering temperature of 1523K × 7.2Ks. A 100% sintered body was obtained.
【００１３】図４に示す顕微鏡組織写真は表１のＨ４成
分組成の圧粉体密度８４％の高合金工具鋼を工具製品形
状に成形した場合、真空焼結１５２３Ｋ，焼結時間７．
２Ｋｓの焼結条件にて焼結したときの微粒粉の配合割合
と空隙、空孔の発生、残留状況を示すものである。即
ち、上段は各微粒粉の配合率に対応する焼結体のラップ
加工面の状況、下段は腐食面を示す顕微鏡組織写真であ
る。これによれば、微粒粉０％、１０％ものは空隙、空
孔等（黒い部分）の残留が認められ、相対密度が１００
％に達していないが、微粒粉が２０％、４０％では相対
密度１００％が得られることが分かる。The microstructure photograph shown in FIG. 4 shows that when a high alloy tool steel of H4 component composition of Table 1 having a green compact density of 84% is formed into a tool product shape, vacuum sintering is 1523 K and sintering time is 7.
It shows the mixing ratio of fine particles, the generation of voids and pores, and the state of residual when sintered under the sintering condition of 2 Ks. That is, the upper part is a microstructure photograph showing the condition of the lapped surface of the sintered body corresponding to the blending ratio of each fine powder, and the lower part is a corroded surface. According to this, fine particles of 0% and 10% have residual voids, voids (black portions), and a relative density of 100%.
Although it has not reached%, it can be seen that a relative density of 100% is obtained when the fine powder is 20% and 40%.
【００１４】[0014]
【発明の効果】本発明は、上述のように粒径が101 〜10
3 μｍ未満の高合金工具鋼の粗粒粉８０〜２０重量％
に、粒径が101 未満で10-2μｍまでの高合金工具鋼の微
粒粉を２０〜８０％配合し、次いでこれを圧粉成形し、
さらに真空雰囲気中で１５２３〜１５５０Ｋｓの温度で
約１２０分間固相焼結処理し、相対密度１００％の緻密
特性を得たので、粉末冶金法の特徴である形状の自由度
を利用して、直接に工具製品形状の工具を固相焼結する
ことができる。しかも、焼結された高合金工具鋼は緻密
化されたので、鍛造、圧延、機械加工を必要とせず、大
幅なコスト低減が可能となった。さらに、結晶粒の粗大
化や炭化物の溶融、凝集に伴う巨大炭化物の形成等の材
料的な組織欠陥や、材料の強靱性及び工具性能を劣化さ
せることもない。As described above, the present invention has a particle size of 10 1 to 10
Coarse-grained powder of high alloy tool steel of less than 3 μm 80 to 20% by weight
20 to 80% of fine powder of high alloy tool steel having a grain size of less than 10 1 and up to 10 -2 μm, and then this is compacted,
Furthermore, solid-state sintering was performed for about 120 minutes at a temperature of 1523 to 1550 Ks in a vacuum atmosphere, and a dense characteristic with a relative density of 100% was obtained. It is possible to solid-phase sinter tools in the form of tool products. Moreover, since the sintered high alloy tool steel is densified, forging, rolling, and machining are not required, and a large cost reduction is possible. Further, it does not cause material structural defects such as coarsening of crystal grains, melting of carbides, formation of giant carbides due to agglomeration, and deterioration of material toughness and tool performance.
【図１】表１に示す本発明に係わる各種の高合金工具鋼
粉末について上段で相対密度５４質量％の、下段で８４
質量％の各圧粉体のそれぞれの焼結温度と焼結体の相対
密度の関係図である。FIG. 1 shows various high alloy tool steel powders according to the present invention shown in Table 1 having a relative density of 54 mass% in the upper stage and 84 in the lower stage.
It is a relationship diagram of each sintering temperature of each green compact of mass%, and the relative density of a sintered compact.
【図２】本発明により得られた焼結体の相対密度の一例
であって、表１の合金成分Ｈ２について粉粒径１０1 〜
１０-2μｍ未満のＦｅ微粉を用いた場合のＦｅ微粉の混
合量と相対密度の関係図である。FIG. 2 is an example of the relative density of the sintered body obtained according to the present invention, in which the particle size of the alloy component H2 in Table 1 is 10 1 to
FIG. 3 is a relationship diagram of the amount of Fe fine powder mixed and the relative density when Fe fine powder of less than 10 −2 μm is used.
【図３】本発明に係わるＨ４の合金粉末の高合金工具鋼
について、粗粒粉と同一成分の高合金工具鋼微粉を混合
したときの相対密度の関係図である。FIG. 3 is a relational diagram of relative densities when a high alloy tool steel of H4 alloy powder according to the present invention is mixed with a coarse alloy powder and a high alloy tool steel fine powder of the same component.
【図４】表１のＨ４の高合金工具鋼の微粒粉の種々の混
合率におけるラップ加工面と腐食面の顕微鏡組織写真で
ある。FIG. 4 is a microstructure photograph of a lapping surface and a corroded surface at various mixing ratios of fine powder of H4 high alloy tool steel in Table 1.
─────────────────────────────────────────────────────
─────────────────────────────────────────────────── ───
【手続補正書】[Procedure amendment]
【提出日】平成３年７月５日[Submission date] July 5, 1991
【手続補正１】[Procedure Amendment 1]
【補正対象書類名】図面[Document name to be corrected] Drawing
【補正対象項目名】図３[Name of item to be corrected] Figure 3
【補正方法】変更[Correction method] Change
【補正内容】[Correction content]
【図３】 [Figure 3]
フロントページの続き (72)発明者 山住 海守 富山県富山市石金20番地 株式会社不二越 内Continued front page (72) Inventor Mamoru Yamazumi 20 Ishigane, Toyama City, Toyama Prefecture Fujikoshi Co., Ltd. Within
Claims (4)
鋼の粗粒粉８０〜２０重量％に、粒径が101 μｍ未満で
10-2μｍまでの高合金工具鋼の微粒粉を２０〜８０％含
み、相対密度１００％の緻密特性を有する高合金工具鋼
焼結体。1. A high-alloy tool steel having a grain size of 10 1 to less than 10 3 μm and 80 to 20% by weight of coarse powder, and a grain size of less than 10 1 μm.
A high alloy tool steel sintered body containing 20 to 80% of fine powder of high alloy tool steel up to 10 -2 µm and having a dense characteristic of a relative density of 100%.
鋼の粗粒粉８０〜２０重量％に、粒径が101 μｍ未満で
10-2μｍまでの高合金工具鋼の微粒粉を２０〜８０％配
合し、次いでこれを圧粉成形し、さらに真空雰囲気中で
１５０３〜１５７３Ｋの温度で約１２０分間固相焼結処
理し、相対密度１００％の緻密特性を得ることを特徴と
する高合金工具鋼焼結体の製造方法。2. A high-alloy tool steel having a grain size of 10 1 to less than 10 3 μm and a coarse grain powder of 80 to 20% by weight, and a grain size of less than 10 1 μm.
20-80% of fine powder of high alloy tool steel up to 10 -2 μm was blended, and then this was compacted and further solid-phase sintered at a temperature of 1503-1573K for about 120 minutes in a vacuum atmosphere, A method for producing a high alloy tool steel sintered body, which is characterized by obtaining a dense property having a relative density of 100%.
する微粉を粗粒粉と同一成分の合金粉末、又は組成中の
単独元素の一種若しくは数種の微粉を混合した請求項２
記載の高合金工具鋼焼結体の製造方法。3. The fine powder to be mixed with the coarse powder of the alloy powder of the high alloy tool steel is an alloy powder having the same composition as the coarse powder, or one or several fine powders of the single element in the composition are mixed.
A method for producing a high alloy tool steel sintered body according to the description.
粉を配合した混合粗粒粉に該混合粗粒粉と同一組成の合
金粉末の微粉又は組成中の単独元素の一種若しくは二種
以上の微粉を配合した混合微粉を混合した請求項２記載
の高合金工具鋼焼結体の製造方法。4. Fine powder of alloy powder having the same composition as said mixed coarse powder, or one or two of the single elements in the composition, in mixed coarse powder mixed with coarse powder of a single element in the components of high alloy tool steel. The method for producing a high alloy tool steel sintered body according to claim 2, wherein mixed fine powders containing one or more kinds of fine powders are mixed.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3187052A JPH059509A (en) | 1991-07-02 | 1991-07-02 | Sintered body of high-alloy tool steel and production thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3187052A JPH059509A (en) | 1991-07-02 | 1991-07-02 | Sintered body of high-alloy tool steel and production thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH059509A true JPH059509A (en) | 1993-01-19 |
Family
ID=16199334
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP3187052A Pending JPH059509A (en) | 1991-07-02 | 1991-07-02 | Sintered body of high-alloy tool steel and production thereof |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH059509A (en) |
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| JP2005533177A (en) * | 2002-07-12 | 2005-11-04 | エクス ワン コーポレーション | Solid-ultra-solid liquid phase sintering of mixed powder |
| WO2012043227A1 (en) * | 2010-09-30 | 2012-04-05 | 日立金属株式会社 | Method for producing molybdenum target |
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| JP2014095136A (en) * | 2012-11-12 | 2014-05-22 | Hirosaki Univ | Superfine powder, high strength steel sintered compact and method for producing them |
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1991
- 1991-07-02 JP JP3187052A patent/JPH059509A/en active Pending
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2005533177A (en) * | 2002-07-12 | 2005-11-04 | エクス ワン コーポレーション | Solid-ultra-solid liquid phase sintering of mixed powder |
| US7070734B2 (en) | 2002-07-12 | 2006-07-04 | The Ex One Company | Blended powder solid-supersolidus liquid phase sintering |
| JP5496078B2 (en) * | 2008-02-26 | 2014-05-21 | Ｊｘ日鉱日石金属株式会社 | Sb-Te alloy powder for sintering, method for producing the same, and sintered body target |
| US8456014B2 (en) | 2008-10-30 | 2013-06-04 | Sony Corporation | Semiconductor device |
| WO2012043227A1 (en) * | 2010-09-30 | 2012-04-05 | 日立金属株式会社 | Method for producing molybdenum target |
| TWI460036B (en) * | 2010-09-30 | 2014-11-11 | 日立金屬股份有限公司 | Method for manufacturing molybdenum target |
| JP5861839B2 (en) * | 2010-09-30 | 2016-02-16 | 日立金属株式会社 | Method for manufacturing molybdenum target |
| US9689067B2 (en) | 2010-09-30 | 2017-06-27 | Hitachi Metals, Ltd. | Method for producing molybdenum target |
| JP2014095136A (en) * | 2012-11-12 | 2014-05-22 | Hirosaki Univ | Superfine powder, high strength steel sintered compact and method for producing them |
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